Heat resistant and wear resistant alloy

ABSTRACT

A heat resistant and wear resistant alloy of the carbidedispersion and precipitation-hardening type, to be used for cutting tools, etc., has a basic composition consisting, in weight percent based on the total weight of said alloy, of from 10 to 90% dispersed particles composed of one or more kinds of carbides or composite carbides of transition metals from Groups 4a, 5a and 6a and the balance being from 50 to 70% Ni, from 2 to 10% Ti, from 0.5 to 10% Al, and one or more kinds of alloy elements selected from the group consisting of from 1 to 10% Fe, from 1 to 20% Co, and from 1 to 20% Cr, said alloy further containing one or more kinds of alloy elements selected from the group consisting, in weight percent based on the weight of a Nibase matrix, of no more than 5% Nb, no more than 10% Ta, no more than 20% Mo, no more than 20% W and no more than 5% V.

United States Patent 1 1 et a1.

[75] Inventors: Hidekazu Doi; Kenichi Nishigaki,

both of Omiya, Japan [73] Assignee: Mitsubishi Metal Corporation,

Tokyo, Japan [22] Filed: Feb. 11, 1974 [21] Appl. No.: 441,125

[30] Foreign Application Priority Data Feb. 16, 1973 Japan 48-18329 [52]U.S. Cl. 29/1823; 29/1827; 75/.5 BC; 75/122; 75/171; 148/325 [51] Int.1C1. C22C 29/00 [58] Field of Search 75/.5 BC, 203, 204, 122, 75/171;29/1827, 182.8, 171; 148/32, 32.5

[56] References Cited UNITED STATES PATENTS 3,502,463 3/1970 Holtz, Jr.75/.5 BC X 3,502,464 3/1970 Holtz, Jr. 75/171 3,576,681 4/1971 Barker eta1... 75/171 X 3,615,376 10/1971 Ross 75/171 3,655,458 4/1972 Reichman75/203 X Prill et a1. 75/203 X Dalal et a1. 75/171 Primary Examiner-L.Dewayne Rutledge Assistant Examiner-Arthur J. Steiner Attorney, Agent,or FirmF1ynn & Frishauf [57] ABSTRACT A heat resistant and wearresistant alloy of the carbide-dispersion and precipitation-hardeningtype, to be used for cutting tools, etc., has a basic compositionconsisting, in weight percent based on the total weight of said alloy,of from 10 to 90% dispersed particles composed of one or more kinds ofcarbides or composite carbides of transition metals from Groups 4a, 5aand 6a and the balance being from 50 to 70% Ni, from 2 to 10% Ti, from0.5 to 10% Al, and one or more kinds of alloy elements selected from thegroup consisting of from 1 to 10% Fe, from 1 to 20% C0, and from 1 to20% Cr, said alloy further containing one or more kinds of alloyelements selected from the group consisting, in weight percent based onthe weight of a Ni-base matrix, of no more than 5% Nb, no more than 10%Ta, no more than 20% Mo, no more than 20% W and no more than 5% V.

8 Claims, 1 Drawing Figure US. Patent Nov. 4, 1975 IOOO- SOO- Q \LPRESENT \QIVENTION /SKH4 260 460 BOO 8C0 IOIOO TEMPERATURE (C) NOTEICOMPOSITION OF ALLOY OF THE PRESENT lNVENTION 20%Ti0- 20% vvc35/o Ni3/Ji(COMPOSITION \N EXAMPLE 4) HEAT RESISTANT AND WEAR RESISTANT ALLOYRELATED APPLICATION This application is related to application Ser. No.441,106, filed Feb. 11, 1974.

The present invention relates to heat-resistant and wear-resistantalloys prepared by utilizing in combination the principles of dispersionstrengthening due to the dispersion of carbide particles and ofprecipitation hardening through the formation of y'-phase [Ni- Al(Ti)]in a Ni-base matrix.

Alloys according to the present invention find their use as materialsfor cutting tools, wear-resisting tools for hot or cold working, etc.Accordingly, the alloys must have high strength and toughness at roomtemperature as well as at elevated temperatures, in addition toexcellent anti-welding properties.

Hitherto, the materials used for cutting tools have been carbon toolsteel, high speed steel, WC base-hard alloy, TiC base cermet, etc.Carbon tool steel and high speed steel are tough but the toughness tendsto'decrease sharply at temperature over about 600C, so the tools made ofsuch materials are used only in a low cutting range within which lessheat is generated.

At increased cutting speeds, the WC base-hard alloys are best, althoughthey suffer from such as being somewhat lower in anti-welding propertiesand in wearresistance. Furthermore, the use of a tool made of suchmaterials in the high speed cutting range gives rise to a demand forgreater resistance to oxidation, because the cutting edge of a tool issubjected to a higher temperature than the rest of the tool. Therefore,within the high speed cutting range TiC base cermet, which has excellentoxidationresistance, finds a wide range of uses.

An alloy according to the present invention is provided as a sinteredtool material, which contains one or more kinds of carbides oftransition metals selected from the Groups 4a, 5a and 6a in the form ofdispersion phase, and the balance of a composition of a Ni-basesuperalloy and is characterized in that the total amount of carbides orcomposite carbides is in the range from 10 to 90%, based on the totalweight of said alloy and the balance thereof is a composition of Ni-basesuper alloy, in which is precipitated a 'y'-phase [Ni Al(Ti)].

The features of the alloy according to the present invention are thatthey retain the high strength and toughness obtained by containing inthe Ni-base matrix high melting point metals, such as Ta, Nb, W, Mo, V,etc. and at the same time do not decrease in strength at a temperatureup to 700C to 800C, due to the excellent heatresistance of the matrixand the high strength of the precipitated 'y-phase at an elevatedtemperature. In addition, alloys of the present invention provide, incombination, excellent high resistance to wear and oxidation as a resultof the carbide phases dispersed in the alloys.

As is clear from the foregoing, the alloys according to the presentinvention are superior in the properties required for tool materials andcan be provided over a wide range of cutting modes, from light to heavy,load by controlling the carbide phase and the amount and nature ofbinder phase in addition they are superior in properties required fortool materials for cold or hot working tools.

Alloys according to the present invention provide excellent cuttingcharacteristics, particularly in the low cutting speed range, in whichhigh speed steel finds its principal application. High speed steel, ingeneral, contains MC, M C and M C type carbides dispersed therein. Thehardness of M C and M C type carbides does not go as high as 1800 to2100 in terms of Vickers hardness. ln contrast thereto, the hardness ofthe principal carbides of the present invention, such as for in- 10stance, TiC, goes as high as 3000 3200 (Vickers hardness). Also, theyhave good wettability to the matrix of Ni base super alloys as well ashigh oxidation resistance. The result is that the excellent propertiesof TiC are well reflected in the cutting performance of tools whichcontain it.

When the alloys of the present invention are used for cutting tools tobe used in a low speed cutting range, the total amount of one or morekinds of carbides or composite carbides contained in the alloy shouldpreferably be in the range of from 20 to On the other hand, the Ni-basesuper alloy matrix functioning as a binding phase in the presentinvention has a basic composition consisting, in weight percent, of from50 to 70% Ni, from 2 to 10% Ti and from 0.5 to 10% Al, said alloyfurther containing one or more kinds of alloy elements selected from thegroup consisting of from 1 to 10% Fe, from 1 to 20% Co, from 1 to 20%Cr, one or more kinds of alloy elements selected from the groupconsisting, in weight percent based on the Ni-matrix, of no more than 5%Nb, no more than 5% V, no more than 10% Ta, no more than 20% Mo and nomore than 20% W.

In this respect, Ti and A] are essential as constituents for forming ay'phase [Ni Al(Ti)] which plays a major role in precipitation-hardening.If the amounts of Ti and A1 are insufficient, less amount of the-y-phase will be precipitated and the resulting alloy will have loweredheatresistance. For this reason, a Ti'content of at least 2% and an Alcontent of at least 0.5% are neces sary. However, if the content of Tiand A] respectively exceed 10%, an undesirable brittle n-phase (Ni Ti)or NiAl phase will be formed. Fe and Co dissolve either in a Ni-matrixor in 'y-phase as solid solution, thereby raising the recrystallizationtemperature. If the Fe or Co content is less than 1%, their effects willbe decreased, while the. Fe content is more than 10% and the Co contentis more than 20%, then the excellent heat resistance of the Ni basematrix will be lowered. Cr dissolves in a Ni-matrix and y'-phase assolid solution, thus improving oxidation-resistance significantly. A Crcontent of less than 1% decreases the effect of Cr, while a Cr contentof more than 20% causes brittleness of the alloy.

W, Mo, Ta, Nb and V each partially dissolve in a Nimatrix, whilepartially forming carbides. These elements dissolved in a Ni-matrixeffectively improve strength of an alloy at elevated temperatures.However, in case the amount of such elements is excessive, the toughnessof the alloy will be decreased. Of these elements, M0 is best to improvethe strength of boundaries of carbide particles and a binding phase,because the Mo added forms Mo-rich composite carbides surrounding thesurface of a starting carbide, which exhibit good affinity to theNi-base binding phase.

The alloy of the present invention may further con tain one or morekinds of alloy elements selected from the group consisting, in weightpercent based on the Nimatrix, of no more than 0.1% B, from 0.01 to 2.0%Zr,

no more than 1% Hf, no more than 0.5% Mg, no more than 1%, in total, ofrare earth elements, (such as La, Y, Ce, etc.), no more than 0.5% P, nomore than 3% Si and no more than 5% Mn.

A small amount of B, Zr, Mg, Hf, P and rare earth elements, if added,gives advantages such as improved deoxidation and desulfurization of theNi-matrix, strengthening of grain boundaries and refining of crystalgrains. However, if the amount of such elements added is excessive, theresult is increased brittleness, because of the formation of compounds.Si and Mn give effects the same as those of B, Zr, Mg, etc. and dissolvein a Ni-matrix, thereby strengthening grain boundaries and improving theeffects of heat treatment. An Si content of over 3% and a Mn content ofover 5% forms compounds, leading to increased brittleness.

Other than the elements above described, the addition, on the basis ofthe total weight of Ni-base matrix, of no more than 1% C, no more than0.1% N, no more than 0.5% Cu, no more than 0.5% Re, no more than 0.5%Ba, no more than 0.5% Rh, or no more than 0.5% Be is effective. Theseelements may be added in place of the aforesaid small amount of elementsor in combination therewith. I

When the amount of C,N, Be, Re, Cu, Rh, etc. added is very small, theydissolve in a Ni-matrix as solid solution, improving the strength of thematrix. However, if too much of such elements is added, brittleness ofthe alloy increases.

When carbide dispersion, precipitation hardening type alloys of thepresent invention are used in a high speed cutting range, higher wearresistance and oxidation resistance are required, as compared with lowspeed cutting. To obtain these properties, a considerable amount of oneor more kinds of carbides or composite carbides of transition metal fromGroups 4, 5a and 6a should be contained in the alloy. More specifically,the total weight of carbides or composite carbides contained in'thealloy should be from 60 to 90% and dispersed in a binding phase of thealloy. In this respect, since y-phase is precipitated in the bindingphase, the strength of the alloy at elevated temperatures will be muchimproved, as compared with the case where precipitated particles are notcontained in the binding phase. More particularly, when comparing theconventional alloy with those of the present invention in terms of theuse of the same amount of binder phase, those according to the presentinvention are much harder at an elevated temperature, so that wearresistance during continuous cutting is improved. Suppose that the wearresistance ofa level the same as that of the conventional alloy isdesired; then the amount of binder phase may be increased, therebyproviding more improved intermittent cutting capability.

Tools which are employed as hot compression dies, hot extrusion punches,hot drawing dies, hot working rolls, hot forging dies, etc. for hotworking are subjected to a high temperature for a relatively long periodof time. Therefore, in addition to the usual resistance against wear andimpact, and creep-resisting and antiwelding properties, they must behard enough to resist softening and deformation at the elevatedtemperature due to the temperature rise during service. For suchapplications, there are among the alloys according to the presentinvention sintered tool materials of Ni-base super alloys containingfrom 10 to 60% by weight of one or more kinds of carbides or compositecarbides of transition metals from Groups 4a, 5a, and 6a, in the formofa dispersion phase and the balance of a composition of a Ni-base superalloy. The prior art carbon tool steel and high speed steel which havebeen widely used tend to soften at a temperature of above 600C and thusare not usable, and in addition such tools present insufficientanti-welding properties.

According to alloys of the present invention, the temperature at whichsoftening starts may be increased to 800C, because the strength of thebinding phase at an elevated temperature is improved due to theprecipitation of a 'y'-phase. Furthermore, alloys according to thepresent invention provide the characteristics required in too] materialsfor hot working, due to the excellent wear resistance and anti-weldingproperties provided by the carbide particles.

The accompanying graph shows hardness at elevated temperatures of analloy of the present invention in comparison with high speed steel(JlS-SKH 4).

The following examples are illustrative of several aspects of thepresent invention. Unless otherwise indicated, the percentage given foralloying elements is weight percent based on total weight of alloy.

EXAMPLE 1 10% WC of a size of 1 was added to 20% TiC powder of 3p. insize which had been obtained by crushing commercially available TiC ofminus mesh in a wet type ball mill. Then the following were added tothis TiC-WC mixture: 35% Ni, 10% Co, 5% Fe, 10% NiAl (Ni Al 7 3), 2% Ti,5% Mo and 3% Cr. These added powdery elements form a binding phase forthe carbide particles. The powder mixture thus prepared was wet-mixed,compacted, sintered under vacuum of 10 mm Hg at 1350C for 1.0 hour. Thesintered product was subjected to solution treatment at 1 C for 4 hoursand thereafter to aging treatment at 750C for 4 hours.

The hardness of the alloy thus obtained was 63 RC (Rockwell C scale).

EXAMPLE 2 The following were added to TiC powder of 3p. in size; 5% Co,40% Ni, 7.9% NiAl (Ni Al 7:3), 2% Ti, 5% Fe, 5% Cr, 5.09% Mo and 0.01%B. These powdery elements form a binding phase for the carbideparticles. The powder mixture thus prepared was wetmixed, compacted,sintered under vacuum at 1350C for 1.0 hour, subjected to solutiontreatment under vacuum at 1 150C for 4 hours, then oil-quenched andtempered at 760C for 3 hours. The hardness of the thus obtained alloyafter measurement was on the Rockwell hardness C scale, 57 aftersintering, 55 after quenching, and 62 after tempering, respectively. Thetransverse rupture strength was 180 kglmm The cutting test results ofsuch tool alloys are shown in Table 1 which shows the superiority of thealloys of the present invention in wear resistance and smoothness offinished surface.

Table 1 Cutting conditions Work Material AlSl 4340 Feed 01 mm/rev. Depthof Cut 1.0 mm Cutting time 2.0 minutes 0.08 good finished Tablel-continued Cutting conditions The following were added to 40% WC powderof 3p. in size and (WTi)C of 3p. in size; 5.09% Co, 30% Ni, 5% NiAl (NiAl 7:3), 3% Cr, 2% Fe, 2.9% Ti, 1% Ta, 001% B and 1% Mn. The powdermixture thus prepared was mixed, compacted, sintered under vacuum of 10'mmHg at 1400C for 1 hour, subjected to solution treatment under vacuumat 1 120C for 4 hours, then oil-quenched, and finally tempered at 800Cfor 4 hours. The hardness of the alloy was as high as 74 on the RockwellC scale, and the transverse rupture strength was 220 kg/mm EXAMPLE 4 Thefollowing were added to powder of 20%, by weight, based on the totalweight of the resulting powder mixture, of TiC of 1 in size and 20% WCof 1 in size; 35% Ni, 3% Ti, 6% NiAl (Ni Al =7 3), 10% Co, 5% M0, 0.5%Si and 0.5% Mn. The powder mixture thus prepared was mixed, compacted,sintered under vacuum at 1350C for 1.0 hour, subjected to solutiontreatment at 1150C for 4 hours, then oil-quenched and finally temperedat 800C for 2 hours. The hardness of the alloy thus obtained was 64 onthe Rockwell C scale, and the transverse rupture strength thereof was210 kg/mm. The hardness of the alloy thus obtained in comparison with ahigh speed steel (JlS, SKH 4) is shown in FIG. 1. The chemicalcomposition of JIS SKI-1 4 is C 0.7 0.85, Si 0.40, Mn 0.40, P 0.03, S0.03, Cr 3.804.5, W 17- 19, V 1 1.5 and C09- 11. It was found that theconventional high speed steel softened at about 600C, whereas thesoftening point of the alloy of the present invention was about 800C.

EXAMPLE 5 The following were added to 60% TiC of 3p. in size, 10% NbC of3p. in size and 5% WC of 1p, in size; 4% Co, 12% Ni, 3.09% NiAl (Ni A1 73), 2% Ti, 1% Fe, 1% Cr, 0.01% B, 1.5% Mo, and 0.4% Ta. The powdermixture thus prepared was wet-mixed, compacted under a pressure of 1t/cm, sintered under vacuum of 10 mmHg at 1400C for 1.0 hour, subjectedto solution treatment at 1120C for 4 hours, then oilquenched and finallytempered at 800C for 2 hours. The hardness of the alloy thus obtainedwas 91.5 on the Rockwell A scale, and the transverse rupture strengththereof was 140 kg/mm".

EXAMPLE 6 The following were added to 15% (TiTa)C, 10% WC and 9% Cr Ceach being of In in size; 40% Ni, 1.8% Ti, 5% NiAl (Ni A1= 7:3), 3.5%Fe, 5% Co, 5% Cr, 5% M0, 0.4% C, 0.5% Mn, and 0.3% Cu. The powder thusprepared was wet-mixed, dried, compacted, sintered under vacuum of 10mmHg at 1350C for 1 hour and cooled in the furnace. The hardness of thealloy thus obtained was 60 on the Rockwell C scale, and the transverserupture strength thereof was 170 6 kg/mm The cutting test reveals thatalloys of the invention are superior to SKH 4.'

EXAMPLE 7 The following were added to 20% (TiZr)C, 5% WC and 5% Mo ceach being of 1p. in size: a Ni-base super alloy powder consisting of50%Ni, 4% Ti, 5% Al, 5% Fe, 10% Co, 10% Cr, 0.3% Be, 7% Mo, 2% Ta and 6.7%W. The powder thus prepared was mechanically mixed, then dried,compacted, sintered under vacuum of 10- mmHg at 1320C for 1 hour,subjected to solution treatment under vacuum at 1120C for 4 hours and,lastly, tempered. The hardness of the alloy thus obtained was about 66on the Rockwell C scale, and the transverse rupture strength thereof was240 kg/mm EXAMPLE 8 The following were added to 30% WC and 10% TaC eachbeing of 1p. in size: 5% C0, 30% Ni, 10% NiAl (Ni :A] 7 :3), 3% Ti, 10%M0, 0.5% C, 1% Si, and 0.5% Mn. The powder thus prepared was mixed,compacted, sintered under vacuum of 10* mmHg at 1380C for 1.0 hour,subjected to solution treatment under vacuum at 1120C for 4 hours,oil-quenched and finally tempered at 800C for 4 hours. The hardness ofthe alloy thus obtained was about 69 R and the transverse rupturestrength thereof was 250 kg/mm EXAMPLE 9 The following were added to 20%(TiZr)C and 10% Mo C each being of 1;; in size: the Ni-base super alloypowder consisting of 50% Ni, 10.08% Cr, 10% Co, 0.3% C, 3% Ti, 5.3% A1,8% Mo, 13% W, 0.01% B, 0.01% Ce and 0.3% Si. The powder thus preparedwas wet-mixed, compacted under a pressure of 1 t/cm, sintered undervacuum of 10 mmHg at 1320C for 1.0 hour, oil-quenched, tempered at 800Cfor 2 hours. The hardness of the alloy thus obtained was 64 R and thetransverse rupture strength thereof was 170 kg/mm.

EXAMPLE 10 The following were added to 50% (TiMo)C, 20% WC and 5% TaCeach being of 1p. in size: 2% Ti, 1.89% Co,15% Ni, 2% Cr, 3% MM (Ni A1 73), 1% M0, 0.1% C and 0.01% B. The powder thus prepared was wet-mixed,compacted, sintered under vacuum at 1370C for 1 hour, subjected tosolution treatment at 1200C for 4 hours, oil-quenched, tempered at 800Cfor 2 hours. The hardness of the alloy thus obtained was 91 R and thetransverse rupture strength thereof was kg/mm.

EXAMPLE 1 1 The following were added to 15% TiC and 5% TaC each being of1p. in size: 45% Ni, 5% Cr, 8% Co, 1.95% Si, 0.05% Cu, 10% MA] (Ni 2 A17 3), 2% Ti, and 8% Mo, which elements were used to form the bindingphase of the present invention. The powder thus prepared was wet-mixed,sintered under vacuum of 10' mmHg at 1320C for 1 hour, subjected tosolution treatment at 1080C for 4 hours, oil-quenched, and finallytempered at 720C for 5 hours. The hardness of the alloy thus obtainedwas 51 R and the transverse rupture strength there' o f was 250 kg/mm.

What we claim is:

A 1. A powder metallurgy sintcred alloy having a basic compositionconsisting essentially of, in weight percent based on the total weightof said alloy, from 10 to 90% of substantially uniformly dispersedpreformed particles composed of at least one carbide or compositecarbide of transition metals of Groups 4a, 5a and 6a and the balance anickel base matrix consisting essentially of from 50 to 70% Ni, from 2to 10% Ti, from 0.5 to 10% Al, at least one alloy element selected fromthe group consisting of from 1 to 10% Fe, from 1 to 20% Co, and from l.to 20% Cr, and at least one alloy element (B), in an amount sufficientto impart high temperature strength, selected from the group consisting,in weight percent based on said Ni-base matrix, of-up to 5% Nb, up to10% Ta, up to 20% Mo, up to 20% W and up to 5% V, and said alloy element(A) dissolving in said Ni-base matrix in the form of a solid solution.

2. An alloy as defined in claim 1, wherein said alloy further containsat least one alloy, element selected from the group consisting, inweight percent based on the Ni-base matrix, of up to 1.0% C, up to 0.1%N, up to 0.5% Cu, up to 0.5% Re, up to 0.5% Ba, up to 0.5% Rh and up to0.5% Be.

. 3. An alloy as defined in claim 5, wherein said alloy further containsat least one alloy element selected from the group consisting, in weightpercent based on the Ni-base matrix, of up to 0.1% B, from 0.01 to 2.0%Zr, up to 1.0% Hf, up to 0.5% Mg, up to 1.0%, in total, of rare earthelements, up to 0.5% P, up to 3.0% Si, and up to 5% Mn.

4. An alloy as defined in claim 3, wherein said alloy further containsat least one alloy element selected from the group consisting, in weightpercent based on Ni-base matrix, of up to 1.0% C, up to 1.0% N, up'to0.5% Cu, up to 0.5% Re, up to 0.5% Ba, up to 0.5% Rh, and up to 0.5% Be.

5. A powder metallurgy sinteredalloy havinga basic compositionconsisting essentially of, in weight percent based on the total weightof said alloy, from 10 to 90% of substantially uniformly dispersedpreformed particles composed of at least one carbide or compositecarbide of transition metals of Groups 4a, 5a and 6a and the balance anickel base matrix consisting essentially of from to 70% Ni, from 2 to10% Ti, from 0.5 to 10% Al, at least one alloy element (A) selected fromthe group consisting of from 1 to 10% Fe, from 1 to 20% Co, and from 1to 5% Cr, and at least one alloy element (B), in an amount sufficient toimpart high temperature strength, selected from the group consisting, inweight percent based on said Ni-base matrix, of up to 5% Nb, up to 10%Ta, up to 20% Mo, up to 20% W and up to 5% V, andsaid alloy element (A)dissolving in said Ni-base matrix in the form of a solid solution.

6. An alloy as defined in claim 5, wherein said alloy further containsat least one alloy element selected from the group consisting, in weightpercent based on the Ni-base matrix, of up to 1.0% C, up to 0.1% N, upto 0.5% Cu, up to 0.5% Re, up to 0.5% Ba, up to 0.5% Rh and up to 0.5%Be.

7. An alloy as defined in claim 5, wherein said alloy further containsat least one alloy element selected from the group consisting, in weightpercent based on the Ni-base matrix, of up to 0.1% B, from 0.1 to 2.0%Zr, up to 1.0% Hf, up to 0.5% Mg, up to 1.0%, in total, of rare earthelements, up to 0.5% P, up to 3.0% Si, and upto5%Mn. I

8. An alloy as defined in claim 7, wherein said alloy further containsat least one element selected from the group consisting, in weightpercentbased on the Nibase matrix, of up to '1 .0% C, up to 1.0% N, upto 0.5% Cu, up to 0.5% Re, up to 0.5% Ba, up to 0.5% Rh, and up to 0.5%Be.

UNITED STATES PATENT OFFICE @TFCATE F EQTTUN PATENT NO. 3,916,497 DATEDNovember 4, 1975 INVENTOR(S) HIDEKAZU DOI et al It is certified thaterror appears in the ab0veidentified patent and that said Letters Patentare hereby corrected as shown below:

Column 1, line 38: replace "oxidationresistance" withoxidation-resistance Column 1, line 56: replace Y with Y' Column 1,after line 38: insert the following as a new paragraph:

-- The accompanying figure shows the influence of alloy composition andtemperature on the hardness of the alloy.

Column 7, line 9: replace "element selected" with element (A) selectedColumn 7, line 25, Claim 3: replace "5" with l Eigned and Sealed this[SEAL] fourth Day Of May 1976 Arrest:

RUTH C. MASON Arresting Officer UNITED STATES PATENT OFFICE fiERHMQATEEQHGN PATENT NO 3,916,497

DATED 1 November 4, 1975 INVENTOR(S) HIDEKAZU DOI et al It is certifiedthat error appears in the above-identified patent and that said LettersPatent are hereby corrected as shown below:

Column 1, line 38: replace "oxidationresistance" withoxidation-resistance Column 1., line 56: replace Y with Y' Column 1,after line 38: insert the following as a new paragraph:

----- The accompanying figure shows the influence of alloy compositionand temperature on the hardness of the alloy.

Column 7, line 9: replace "element selected" with element (A) selectedColumn 7, line 25, Claim 3: replace "5" with l and gril this fourth DayOf May 1976 [SEAL] Attesi:

RUTH C. MASON Allvsting Officer

1. A POWDER METALLURGY SINTERED ALLOY HAVING A BASIC COMPOSITIONCONSISTNG ESSENTIALLY OF, IN WEIGHT PERCENT BASED ON THE TOTAL WEIGHT OFSAID ALLOY, FROM 10 TO 90% OF SUBSTANTIALLY UNIFORMYL DISPERSEDPREFORMED PARTICLES COMPOSED OF AT LEAST ONE CARBODE OR COMPOSITECARBIDE OF TRANSITION METALS OF GROUPS 4A, 5A AND 6A AND THE BALANCE ANICKEL BASE MATRIX CONSISTING ESSENTIALLY OF FROM 50 TO 70% NI, FROM 2TO 10% TI, FROM 0.5 TO 10% AL, AT LEAST ONE ALLOY ELEMENT SELECTED FROMTHE GROUP CONSISTING OF FROM 1 TO 10% FE, FROM 1 TO 20% CO, AND FROM 1TO 20% CR, AND AT LEAST ONE ALLOY ELEMENT (B) IN AN AMOUNT SUFFICIENT TOIMPART HIGH TEMPERATURE STRENGTH, SELECTED FROM THE GROUP CONSSING , INWEIGHT PERCENT BASED ON SAID NI-BASE MATRIX, OF UP TO 5% NB, UP TO 10%TA, UP TO 20% MO, UP TO 20% W AND UP TO 5% V, AND SAID ALLOY ELEMENT (A)DISSOLVING IN SAID NI-BASE MATRIX IN THE FORM OF A SOLID SOLUTION
 2. Analloy as defined in claim 1, wherein said alloy further contains atleast one alloy element selected from the group consisting, in weightpercent based on the Ni-base matrix, of up to 1.0% C, up to 0.1% N, upto 0.5% Cu, up to 0.5% Re, up to 0.5% Ba, up to 0.5% Rh and up to 0.5%Be.
 3. An alloy as defined in claim 5, wherein said alloy furthercontains at least one alloy element selected from the group consisting,in weight percent based on the Ni-base matrix, of up to 0.1% B, from0.01 to 2.0% Zr, up to 1.0% Hf, up to 0.5% Mg, up to 1.0%, in total, ofrare earth elements, up to 0.5% P, up to 3.0% Si, and up to 5% Mn.
 4. Analloy as defined in claim 3, wherein said alloy further contains atleast one alloy element selected from the group consisting, in weightpercent based on Ni-base matrix, of up to 1.0% C, up to 1.0% N, up to0.5% Cu, up to 0.5% Re, up to 0.5% Ba, up to 0.5% Rh, and up to 0.5% Be.5. A powder metallurgy sintered alloy having a basic compositionconsisting essentially of, in weight percent based on the total weightof said alloy, from 10 to 90% of substantially uniformly dispersedpreformed particles composed of at least one carbide or compositecarbide of transition metals of Groups 4a, 5a and 6a and the balance anickel base matrix consisting essentially of from 50 to 70% Ni, from 2to 10% Ti, from 0.5 to 10% Al, at least one alloy element (A) selectedfrom the group consisting of from 1 to 10% Fe, from 1 to 20% Co, andfrom 1 to 5% Cr, and at least one alloy element (B), in an amountsufficient to impart high temperature strength, selected from the groupconsisting, in weight percent based on said Ni-base matrix, of up to 5%Nb, up to 10% Ta, up to 20% Mo, up to 20% W and up to 5% V, and saidalloy element (A) dissolving in said Ni-base matrix in the form of asolid solution.
 6. An alloy as defined in claim 5, wherein said alloyfurther contains at least one alloy element selected from the groupconsisting, in weight percent based on the Ni-base matrix, of up to 1.0%C, up to 0.1% N, up to 0.5% Cu, up to 0.5% Re, up to 0.5% Ba, up to 0.5%Rh and up to 0.5% Be.
 7. An alloy as defined in claim 5, wherein saidalloy further contains at least one alloy element selected from thegroup consisting, in weight percent based on the Ni-base matrix, of upto 0.1% B, from 0.1 to 2.0% Zr, up to 1.0% Hf, up to 0.5% Mg, up to1.0%, in total, of rare earth elements, up to 0.5% P, up to 3.0% Si, andup to 5% Mn.
 8. An alloy as defined in claim 7, wherein said alloyfurther contains aT least one element selected from the groupconsisting, in weight percent based on the Ni-base matrix, of up to 1.0%C, up to 1.0% N, up to 0.5% Cu, up to 0.5% Re, up to 0.5% Ba, up to 0.5%Rh, and up to 0.5% Be.